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WO2009096611A1 - Composition de verre pour substrat - Google Patents

Composition de verre pour substrat Download PDF

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Publication number
WO2009096611A1
WO2009096611A1 PCT/JP2009/053440 JP2009053440W WO2009096611A1 WO 2009096611 A1 WO2009096611 A1 WO 2009096611A1 JP 2009053440 W JP2009053440 W JP 2009053440W WO 2009096611 A1 WO2009096611 A1 WO 2009096611A1
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WO
WIPO (PCT)
Prior art keywords
glass
substrate
cao
sro
substrates
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Ceased
Application number
PCT/JP2009/053440
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English (en)
Japanese (ja)
Inventor
Kensuke Nagai
Tetsuya Nakashima
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
AGC Inc
Original Assignee
Asahi Glass Co Ltd
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Asahi Glass Co Ltd filed Critical Asahi Glass Co Ltd
Priority to EP09706784.7A priority Critical patent/EP2246310B1/fr
Priority to JP2009551641A priority patent/JP5392096B2/ja
Priority to CN2009801069980A priority patent/CN101959819A/zh
Priority to KR1020107011505A priority patent/KR101273782B1/ko
Publication of WO2009096611A1 publication Critical patent/WO2009096611A1/fr
Priority to US12/769,703 priority patent/US8349751B2/en
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

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Classifications

    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01J—ELECTRIC DISCHARGE TUBES OR DISCHARGE LAMPS
    • H01J11/00—Gas-filled discharge tubes with alternating current induction of the discharge, e.g. alternating current plasma display panels [AC-PDP]; Gas-filled discharge tubes without any main electrode inside the vessel; Gas-filled discharge tubes with at least one main electrode outside the vessel
    • H01J11/20—Constructional details
    • H01J11/34—Vessels, containers or parts thereof, e.g. substrates
    • C—CHEMISTRY; METALLURGY
    • C03—GLASS; MINERAL OR SLAG WOOL
    • C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
    • C03C3/00—Glass compositions
    • C03C3/04—Glass compositions containing silica
    • C03C3/076—Glass compositions containing silica with 40% to 90% silica, by weight
    • C03C3/083—Glass compositions containing silica with 40% to 90% silica, by weight containing aluminium oxide or an iron compound
    • C03C3/085—Glass compositions containing silica with 40% to 90% silica, by weight containing aluminium oxide or an iron compound containing an oxide of a divalent metal
    • C03C3/087—Glass compositions containing silica with 40% to 90% silica, by weight containing aluminium oxide or an iron compound containing an oxide of a divalent metal containing calcium oxide, e.g. common sheet or container glass
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01J—ELECTRIC DISCHARGE TUBES OR DISCHARGE LAMPS
    • H01J5/00—Details relating to vessels or to leading-in conductors common to two or more basic types of discharge tubes or lamps
    • H01J5/02—Vessels; Containers; Shields associated therewith; Vacuum locks
    • H01J5/04—Vessels or containers characterised by the material thereof

Definitions

  • the present invention relates to a glass composition for a substrate which is useful as a substrate for a flat panel display (hereinafter abbreviated as FPD), particularly as a substrate for a plasma display panel (hereinafter abbreviated as PDP) and has excellent polishing properties. Furthermore, it is related with the glass composition for substrates which suppresses yellowing.
  • FPD flat panel display
  • PDP plasma display panel
  • a PDP is generally manufactured by baking a metal electrode, an insulating paste, a rib paste, etc. on a substrate glass at a temperature of about 550 to 600 ° C., and then frit-sealing the counter plate and the periphery.
  • soda lime silica glass widely used for construction or automobiles has been generally used as glass for PDP substrates.
  • Patent Document 1 a glass composition for a substrate having a thermal expansion coefficient close to that of soda lime silica glass and a high glass transition point and strain point is known (see Patent Document 1). ).
  • the FPD substrate glass is sometimes chamfered (polished) for the purpose of preventing breakage and the like.
  • polishing may be performed for the reduction
  • conventional glass for substrates is poor in workability in polishing work, and easily causes problems such as a decrease in productivity and an increase in manufacturing cost.
  • the glass composition is simply excellent in polishing properties. That is, it is difficult to make the characteristics such as the glass transition point, the thermal expansion coefficient, the volume resistivity, the high temperature viscosity, and the specific gravity within the range to be satisfied as the substrate glass for PDP.
  • the present invention aims to provide a glass composition for a substrate that is excellent in polishing properties and can be produced with high productivity while ensuring the characteristics and quality as a substrate for PDP. . Furthermore, this invention aims at providing the glass composition for substrates which suppresses yellowing. Yellowing refers to a phenomenon in which a silver electrode for discharging plasma is baked and formed on the glass substrate surface, whereby the glass substrate surface turns yellow.
  • the present invention is expressed in terms of mass% based on oxide, and as a glass mother composition, SiO 2 55-75% Al 2 O 3 5-15% MgO 0-4% CaO 5.5% more than 12% or less SrO 5-18% BaO 0-13% ZrO 2 0.5-6% Na 2 O 0-10% K 2 O 0-15% Na 2 O + K 2 O 6-20% MgO + CaO + SrO + BaO 17-25% CaO + SrO 15-25% Consists of For substrates characterized by having a glass transition point of 600 ° C. or higher, an average coefficient of thermal expansion at 50 to 350 ° C. of 75 ⁇ 10 ⁇ 7 to 90 ⁇ 10 ⁇ 7 / ° C., and a degree of wear of 98 or higher. A glass composition is provided.
  • the glass composition for a substrate of the present invention provides a glass for a substrate that can be produced at a low cost with excellent polishing properties while ensuring the characteristics as an FPD substrate, particularly a PDP substrate. Can do. Furthermore, it is possible to obtain a glass for a substrate that hardly causes yellowing. Moreover, since the glass composition for substrates of the present invention has a high transition point and excellent thermal stability and is easy to process such as polishing, it can be used effectively as glass for solar cell substrates.
  • FIG. 1 is a schematic cross-sectional view of an end portion of a chamfered substrate glass.
  • Substrate glass 12 Chamfered portion T Thickness of substrate glass
  • the glass composition for substrates of the present invention is expressed in terms of mass% based on oxide, and as a glass mother composition, SiO 2 55-75% Al 2 O 3 5-15% MgO 0-4% CaO 5.5% more than 12% or less SrO 5-18% BaO 0-13% ZrO 2 0.5-6% Na 2 O 0-10% K 2 O 0-15% Na 2 O + K 2 O 6-20% MgO + CaO + SrO + BaO 17-25% CaO + SrO 15-25% Consists of.
  • SiO 2 A component that forms a glass skeleton. If it is less than 55%, the glass heat resistance deteriorates. If it exceeds 75%, the coefficient of thermal expansion will decrease, and the high temperature viscosity of the glass will increase and the solubility may deteriorate.
  • the content of SiO 2 is preferably 55 to 65%. More preferably, it is 55 to 60%, and still more preferably 55 to 57%.
  • Al 2 O 3 The effect of increasing the glass transition point and improving the heat resistance is less than 5%. On the other hand, if it exceeds 15%, the high temperature viscosity of the glass increases and the solubility decreases.
  • the content of Al 2 O 3 is preferably 5 to 10%. More preferably, it is 5 to 8%, and further preferably 5 to 7%. Further, considering the suppression of yellowing, it is more preferably 8 to 10%.
  • MgO When it is 0 to 4%, it has an action of lowering the viscosity at the time of melting the glass and promoting the melting. When this content rate is higher than 4%, the polishability of the obtained glass for a substrate may be lowered.
  • the MgO content is preferably 0 to 3.5%. More preferably, it is 0 to 3%.
  • the CaO content is preferably 6 to 10%. More preferably, it is 6 to 8%, and further preferably 6 to 7.5%. Considering suppression of yellowing, it is preferably 5.8 to 10%. More preferably, it is 5.8 to 8%, and still more preferably 5.8 to 7.5%.
  • the SrO content is preferably 8 to 15%. More preferably, it is 8 to 13%, and further preferably 9 to 12%.
  • BaO Similar to BaO: CaO and SrO, if it is 13% or less, it has the effect of improving the polishability of the glass for substrates, improving the glass transition point and increasing the thermal expansion coefficient, and reducing the high temperature viscosity of the glass. Can be made. However, if its content exceeds 13%, the thermal expansion coefficient of the glass becomes too large and the specific gravity becomes too heavy, so it is 13% or less.
  • the BaO content is preferably 10% or less. More preferably, it is 9% or less, More preferably, it is 8% or less. In view of environmental load, it is particularly preferable that BaO is not substantially contained.
  • MgO + CaO + SrO + BaO If these are less than 17% in total, the high-temperature viscosity of the glass will increase too much and the glass transition point will be too low. On the other hand, if the total amount exceeds 25%, the specific gravity is too large. The total amount of these is preferably 18 to 25%, more preferably 19 to 25%.
  • CaO + SrO + BaO When the total amount of CaO + SrO: CaO + SrO + BaO is less than 15%, the polishability of the glass for substrates cannot be improved. Moreover, the high-temperature viscosity of glass rises too much and a glass transition point becomes too low. On the other hand, if the total amount exceeds 25%, the specific gravity is too large. Among these, CaO + SrO is 15 to 25% because the polishability of the substrate glass is further improved. It is preferably 15 to 23%, more preferably 15 to 20%.
  • Na 2 O + K 2 O In order to obtain a predetermined thermal expansion coefficient, at least one kind is essential. If the total amount is less than 6%, the thermal expansion coefficient is too small. On the other hand, if the total amount exceeds 20%, the heat resistance of the glass decreases.
  • the total amount of these is preferably 7 to 17%, more preferably 7 to 15%. Considering suppression of yellowing, it is preferably 7 to 14%, more preferably 7 to 13%.
  • Na 2 O is 0 to 10%
  • K 2 O is 0 to 15%.
  • a Na 2 O content of 2 to 10% and a K 2 O content of 1 to 13% are preferred because the polishing properties of the substrate glass are further improved. Yellowing considering that inhibit the Na 2 O is 2-8%, preferably a K 2 O is 1-10%, a Na 2 O is 3 ⁇ 8% K 2 O 1. More preferably, it is 5 to 10%.
  • Li 2 O contains substantially no unavoidable impurities in order to lower the heat resistance of the glass.
  • ZrO 2 Used for improving the heat resistance and chemical durability of glass, but less than 0.5% has little effect. On the other hand, if the content exceeds 6%, the devitrification temperature of the glass becomes too high and the thermal expansion coefficient becomes too low.
  • the content of ZrO 2 is preferably 1 to 5%. More preferably, it is 1 to 4%, and further preferably 1 to 3.5%.
  • the glass composition for a substrate of the present invention is expressed in mass% on an oxide basis, and as a glass mother composition, SiO 2 55-65% Al 2 O 3 5-10% MgO 0-3.5% CaO 5.8-10% SrO 8-15% BaO 0-10% ZrO 2 1-5% Na 2 O 2-10% K 2 O 1-13% Na 2 O + K 2 O 7-17% MgO + CaO + SrO + BaO 18-25% CaO + SrO 15-23% Preferably it consists of.
  • the glass composition for a substrate is a glass mother composition.
  • the additive contains 0.06 to 0.15% of Fe 2 O 3 as an additive.
  • the solubility may contain B 2 O 3. However, if contained excessively, the coefficient of thermal expansion of the substrate glass becomes too low, so it is preferable to make it less than 1.5%. Moreover, it is more preferable that the glass composition for substrates of the present invention does not substantially contain B 2 O 3 .
  • a SO 3 as a fining agent.
  • a SO 3 source it is preferable to add a sulfate such as potassium sulfate (K 2 SO 4 ), sodium sulfate (Na 2 SO 4 ), calcium sulfate (CaSO 4 ) to the glass raw material.
  • a part of SO 3 added as a fining agent may remain.
  • the addition amount is 10 parts by mass with respect to the glass matrix composition raw material 100 parts by weight SO 3, would be separated from the glass melt during the dissolution , It will not melt. Further, if it is less than 0.5 parts by mass, the clarification effect is poor. For this reason, it is preferable to add 0.5 to 10 parts by mass. 0.5 to 8 parts by mass is more preferable, further preferably 0.5 to 4 parts by mass, and particularly preferably 0.7 to 2 parts by mass (hereinafter referred to as “parts by mass”). It means the addition amount with respect to 100 parts by mass).
  • the residual amount (content) in terms of SO 3 in the glass composition for substrates is preferably 0.001 to 0.6%, more preferably 0.002 to 0.5%, more preferably 0.00% in terms of mass%. 005 to 0.4% is more preferable, and 0.01 to 0.4% is particularly preferable.
  • the glass composition for a substrate of the present invention improves the solubility, clarity, and formability of the glass, so that SnO 2 , As 2 O 3 , Sb 2 O 3 ,
  • the total amount of P 2 O 5 , F, and Cl is preferably 2 parts by mass or less, more preferably 1.5 parts by mass or less.
  • additives are added so that the total amount of La 2 O 3 , TiO 2 , SnO 2 and ZnO is 5 parts by mass or less with respect to the glass matrix composition raw material. May be.
  • a colorant such as Fe 2 O 3 , CoO, NiO, or Nd 2 O 3 may be added.
  • a coloring agent may be added so that it may become 3 mass parts or less with respect to a glass mother composition raw material, and it is preferable to add so that it may become 1 mass part or less.
  • Fe 2 O 3 is contained as an additive in an amount of 0.06% or more.
  • Fe 2 O 3 to inhibit the varying glass yellow is contained 0.15% or less.
  • Fe 2 O 3 is preferably contained in an amount of 0.06 to 0.14%, more preferably 0.07 to 0.13%, still more preferably 0.08 to 0.12%.
  • the glass substrate of the glass composition of the present invention has an average content of Fe 2+ in the surface layer from the glass substrate surface on the side on which the silver electrode is formed to a depth of 10 ⁇ m. It is preferably 0.0725% or less in terms of Fe 2 O 3 .
  • the glass composition for substrates of the present invention preferably has a high temperature viscosity lower than that of conventional glass for PDP substrates.
  • the glass melt temperature T 2 corresponding to a viscosity of 10 2 dPa ⁇ s is preferably 1570 ° C. or lower.
  • the viscosity of 10 2 dPa ⁇ s is a reference viscosity indicating that the viscosity of the glass melt is sufficiently low. Accordingly, the temperature T 2 at which the viscosity of the glass melt is 10 2 dPa ⁇ s is the reference temperature of the glass melt.
  • the glass composition for substrates of the present invention can be subjected to the melting step at a low temperature. As a result, stable production of glass becomes possible.
  • T 2 is preferably 1560 ° C. or less, more preferably 1550 ° C. or less, further 1540 ° C. or less, and particularly preferably 1500 ° C. or less.
  • the glass melt temperature T 4 corresponding to a viscosity of 10 4 dPa ⁇ s is preferably 1200 ° C. or lower.
  • the viscosity of 10 4 dPa ⁇ s is a reference viscosity when glass is float formed. Accordingly, the temperature T 4 at which the viscosity of the glass melt becomes 10 4 dPa ⁇ s is also the reference temperature of the glass melt in the float forming process.
  • the glass composition for substrates of the present invention can carry out the float forming process at a lower temperature than before. As a result, stable molding of the glass becomes possible. In addition, the life of the float bath is extended. Further, since the fuel required to heat the float tank is reduced, the manufacturing cost of the substrate glass is reduced. Moreover, since the temperature of the glass ribbon drawn out from the float tank becomes low, the energy required for the slow cooling step performed following the float forming is reduced.
  • the glass composition for substrates of the present invention has an average coefficient of thermal expansion at 50 to 350 ° C. in the range of 75 ⁇ 10 ⁇ 7 to 90 ⁇ 10 ⁇ 7 / ° C.
  • a frit material or a paste material used when producing the PDP must be one that corresponds to the thermal expansion coefficient of the glass.
  • the glass composition for a substrate of the present invention preferably has a thermal expansion coefficient in the range of 80 ⁇ 10 ⁇ 7 to 90 ⁇ 10 ⁇ 7 / ° C.
  • the glass composition for a substrate of the present invention preferably has a specific gravity of 2.9 or less. If the specific gravity is more than 2.9, the glass composition for a substrate becomes heavy, which is not preferable for handling and particularly for transportation.
  • the specific gravity of the glass composition for a substrate being 2.9 or less is a particularly important characteristic for a large substrate.
  • the glass composition for a substrate of the present invention preferably has a specific gravity of 2.8 or less, more preferably 2.75 or less.
  • the glass composition for substrates of the present invention has a glass transition point Tg of 600 ° C. or higher.
  • Tg glass transition point
  • the shrinkage amount of the glass due to the heat treatment is not sufficiently reduced when a large PDP such as a nominal 40 inch is manufactured.
  • Tg glass transition point 615 degreeC or more, More preferably, it is 630 degreeC or more.
  • 640 degreeC or more, especially 650 degreeC or more are preferable.
  • the glass composition for substrates of the present invention preferably has a volume resistivity at 150 ° C. of 10 11 ⁇ ⁇ cm or more.
  • a silver electrode is formed on the surface of the substrate glass.
  • the substrate glass composition is preferably excellent in insulation.
  • the volume resistivity at 150 ° C. is 10 11 ⁇ ⁇ cm or more, the insulation is excellent, and even when the PDP is enlarged or densified, the silver electrode formed on the substrate glass is energized. There is no possibility that part of the current that is energized flows through the glass around the silver electrode.
  • the composition of the glass composition for a substrate is selected by focusing only on lowering the high-temperature viscosity, it is difficult to increase the volume resistivity at 150 ° C. to 10 11 ⁇ ⁇ cm or more.
  • the high temperature viscosity of the glass can be lowered while keeping the volume resistivity of the glass at 150 ° C. at 10 11 ⁇ ⁇ cm or more.
  • the volume resistivity of the glass at 150 ° C. is preferably 2 ⁇ 10 11 ⁇ ⁇ cm or more, and more preferably 5 ⁇ 10 11 ⁇ ⁇ cm or more.
  • the glass composition for a substrate of the present invention has a degree of wear (FA) which is one of the measures of polishability of 98 or more. Therefore, the workability of chamfering (edge polishing) for the purpose of preventing breakage such as breakage or chipping of the glass is high. Therefore, productivity can be improved and manufacturing cost can be reduced. In addition, the chamfering quality is improved and the yield is improved by reducing the breakage rate. In addition, the workability of polishing the glass surface for the purpose of preventing silver coloration during electrode formation on the glass surface is high. Therefore, productivity can be improved and manufacturing cost can be reduced.
  • the substrate glass of the present invention has a degree of wear (FA) of preferably 100 or more, more preferably 105 or more, and particularly preferably 105 to 150.
  • the degree of wear shall mean the measured value as follows.
  • a sample having a measurement area of 9 cm 2 whose mass has been measured in advance is held on the surface of a disk-shaped flat plate made of cast iron at a position 80 mm from the center. Then, in a state where it is rotated at 60 times / minute while maintaining a horizontal state, a lapping solution obtained by adding alumina abrasive grains having an average particle diameter of 20 ⁇ m to 20 ml of water is uniformly supplied for 5 minutes. . Next, after wrapping with a load of 9.807 N, the mass is measured. Then, the wear mass m is determined from the difference in mass before and after the lap. Then, the same operation is performed for the Japan Optical Glass Industry Association specified in the standard sample (BSC7), similarly determine the abrasion mass m 0. Then, the degree of wear (FA) is obtained from the following equation.
  • d means the specific gravity of the sample
  • d 0 means the specific gravity of the standard sample (BSC7). This specific gravity means a value measured by the Archimedes method using pure water.
  • the chamfering means that the edge portion generated at the end portion is polished after cutting the substrate glass into a desired size, and the chamfered cross section 12 is circularly formed so as to drop the corner as shown in FIG.
  • the shape is not limited to the arc shape, but may be other shapes).
  • the method for chamfering is not particularly limited.
  • the edge of the glass sheet can be chamfered using a rotating wheel with abrasive grains in which abrasive grains are provided on the peripheral surface of the rotating wheel as in a conventionally known method.
  • the polishing of the substrate glass surface for the purpose of preventing silver color development will be described.
  • a silver paste is baked on the surface of a substrate glass having a reduction layer on the surface to form a silver electrode, the surface may be discolored, and thus the reduction layer may be polished and removed.
  • the method for polishing is not particularly limited.
  • the surface of the substrate glass can be polished by using cerium oxide or the like as an abrasive as in a conventionally known method and using an Oscar type polishing machine.
  • a plate glass in connection with polishing, a plate glass can be ground using a core drill with abrasive grains provided with an abrasive grain portion at the tip of a rotating core, and holes can be easily formed.
  • the glass composition for a substrate of the present invention preferably has a crack depth of 37 ⁇ m or more when the Vickers indenter is pushed in with a load of 200 g as another measure of the polishing property. Also in this case, chamfering, polishing and perforation can be easily performed. However, when considered as a scale, the above degree of wear is preferable to the polishing rather than the crack depth.
  • the depth of the crack is measured by vertically cutting an indentation formed by pressing a Vickers indenter and measuring the vertical crack depth at the end face. In the glass for a substrate of the present invention, the depth of the crack is more preferably 39 to 100 ⁇ m.
  • a yellow paste b * on the glass surface after the silver paste is removed after the silver paste is applied and baked on the glass surface Is preferably 4 or less, more preferably 3.5 or less, and particularly preferably 0 to 3.
  • the glass for a substrate of the present invention can be used to produce a glass for a substrate, for example, by the following method. That is, the raw materials of each component that are usually used are prepared so as to become target components, which are continuously fed into a melting furnace, heated and melted at 1200 to 1400 ° C., and clarified at 1400 to 1700 ° C. The molten glass is formed into a predetermined plate thickness by the float method, and is cooled and then cut to obtain a transparent glass substrate.
  • Table 1 shows the glass compositions of Examples 1 to 5 (Examples), Examples 6 to 8 (Comparative Examples), and Table 2 shows Examples 9 to 13 (Examples).
  • a raw material was prepared so as to have a matrix composition (SiO 2 to Zr 2 O) described in Tables 1 and 2 and containing the additive described in Table 2, and sulfuric acid was added to 100 parts by mass of the raw material. 0.8 parts by mass of salt in terms of SO 3 was added to obtain a glass raw material, and the glass raw material was melted by heating at a temperature of 1500 to 1600 ° C. for 4 hours using a platinum crucible. For melting, a platinum stirrer was inserted and stirred for 2 hours to homogenize the glass.
  • the glass melt was poured out, slowly cooled, and then polished to form a plate having a thickness of 2.8 mm.
  • the glass composition (mass%), the glass transition point Tg (° C.), the average thermal expansion coefficient ⁇ 50-350 (10 ⁇ 7 / ° C.) at 50 to 350 ° C., the volume resistivity at 150 ° C. ⁇ ( ⁇ ⁇ cm), T 2 (° C.), T 4 (° C.), specific gravity (g / cm 3 ), degree of wear and crack depth ( ⁇ m) were measured.
  • the results are shown in Tables 1 and 2.
  • the residual amount of SO 3 in the glass was 0.05 to 0.3% by mass.
  • the value in parentheses in the table indicates the calculated value.
  • the average coefficient of thermal expansion at 50 to 350 ° C. is a value measured by using a differential thermal dilatometer (TMA), and is a value obtained by JIS R3102 (1995).
  • the glass transition point is a value measured using TMA, and was determined according to JIS R3103-3 (FY2001).
  • the volume resistivity was calculated by measuring the value of the current flowing in the glass when 100 V was applied by an electrode using a three-terminal method.
  • T 2 and T 4 are the temperatures T 2 when the viscosities of the compositions similar to those of Examples 1 to 13 are measured using a rotational viscometer, and the glass of Examples 1 to 13 has a viscosity of 10 2 dPa ⁇ s.
  • the temperature T 4 when 10 4 dPa ⁇ s was obtained was calculated by a weighted average.
  • the glass transition point was determined as follows. The glass was held at the temperature of the annealing point for 30 minutes and then slowly cooled at a cooling rate of 60 ° C./min. Next, for this slowly cooled glass, a differential thermal dilatometer was used to obtain a curve of thermal expansion coefficient with respect to temperature from room temperature to the yield point. A tangent line was drawn before and after the first bending point of this curve, and the temperature corresponding to the intersection of the tangent lines was taken as the glass transition point. The b * value was determined as follows. The glass obtained above was melted, poured into a plate shape, gradually cooled, and both surfaces were mirror-polished to obtain a plate glass having a thickness of 2.8 mm.
  • the glasses of Examples have an abrasion degree of 98 or more and excellent polishing properties. Furthermore, the glass transition point is 600 ° C. or higher, the thermal expansion coefficient is 75 ⁇ 10 ⁇ 7 / ° C. to 90 ⁇ 10 ⁇ 7 / ° C., and the volume resistivity ⁇ is 10 11 ⁇ ⁇ cm or higher. Suitable as substrate glass.
  • Example 6 CaO is 5.5% or less, and CaO + SrO is less than 15%, so the degree of wear is low.
  • Example 7 since SrO is less than 5% and CaO + SrO is less than 15%, the degree of wear is low. Therefore, the productivity of the glasses of Examples 6 to 8 is reduced.
  • the glasses of Examples 9 to 13 had b * of 4 or less, and yellowing hardly occurred.
  • a raw material is prepared so that it may become the glass composition of this invention, and it melt
  • chamfering of the glass end for the purpose of preventing breakage or the like is performed.
  • the glass surface is polished to remove the reducing layer on the glass surface.
  • the glass for a substrate having the composition of the present invention can efficiently chamfer (polish) the edge of the glass. Moreover, the glass surface can be polished efficiently. As a result, the target substrate glass can be manufactured with high productivity and low cost.
  • the glass composition for substrates of the present invention is suitable as a substrate for FPD, particularly as a substrate for PDP.
  • the substrate glass composition of the present invention can also be used as a magnetic disk substrate.

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Abstract

L'invention porte sur une composition de verre pour substrats qui possède une bonne aptitude à être polie tout en conservant les caractéristiques requises par les substrats FPD, en particulier par les substrats PDP. La composition de verre pour substrat selon l'invention permet de former un verre pour substrat possédant d'excellentes qualités de productivité et d'ouvrabilité au cours du processus de polissage. La composition de verre pour substrat précitée est caractérisée en ce qu'elle contient une matrice de verre composée, en % massique sur la base des oxydes, de 55 à 75% de SiO2, de 5 à 15% d'Al2O3, de 0 à 4% de MgO, de plus de 5,5% à 12% maximum de CaO, de 5 à 18% de SrO, de 0 à 13% de BaO, de 0,5 à 6% de ZrO2, de 0 à 10% de Na2O, de 0 à 15% de K2O, de 6 à 20% de Na2O + K2O, de 17 à 25% de MgO + CaO + SrO + BaO, et de 15 à 25% de CaO + SrO. La composition de verre pour substrat est également caractérisée en ce qu'elle possède une température de transition vitreuse d'au moins 600˚C, un coefficient d'expansion thermique moyen dans la plage de températures de 50 à 350˚C compris entre 75 × 10-7/˚C et 90 × 10-7/˚C, et un degré d'abrasion d'au moins 98.
PCT/JP2009/053440 2008-02-27 2009-02-25 Composition de verre pour substrat Ceased WO2009096611A1 (fr)

Priority Applications (5)

Application Number Priority Date Filing Date Title
EP09706784.7A EP2246310B1 (fr) 2008-02-27 2009-02-25 Composition de verre pour substrat
JP2009551641A JP5392096B2 (ja) 2008-02-27 2009-02-25 基板用ガラス組成物
CN2009801069980A CN101959819A (zh) 2008-02-27 2009-02-25 基板用玻璃组合物
KR1020107011505A KR101273782B1 (ko) 2008-02-27 2009-02-25 기판용 유리 조성물
US12/769,703 US8349751B2 (en) 2008-02-27 2010-04-29 Glass composition for substrates

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2008046356 2008-02-27
JP2008-046356 2008-02-27

Related Child Applications (1)

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US12/769,703 Continuation US8349751B2 (en) 2008-02-27 2010-04-29 Glass composition for substrates

Publications (1)

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WO2013099768A1 (fr) * 2011-12-27 2013-07-04 旭硝子株式会社 Substrat de verre et procédé de fabrication d'un substrat de verre
JP2015187079A (ja) * 2010-07-26 2015-10-29 旭硝子株式会社 Ｃｕ−Ｉｎ−Ｇａ−Ｓｅ太陽電池用ガラス基板及びそれを用いた太陽電池
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JP6584013B2 (ja) 2013-08-15 2019-10-02 コーニング インコーポレイテッド Ｃｔｅが中程度から高いガラスおよびそれを備えたガラス物品
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EP4361112A3 (fr) 2018-11-26 2024-12-11 Owens Corning Intellectual Capital, LLC Composition de fibre de verre à haute performance à module élastique amélioré
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JP2015187079A (ja) * 2010-07-26 2015-10-29 旭硝子株式会社 Ｃｕ−Ｉｎ−Ｇａ−Ｓｅ太陽電池用ガラス基板及びそれを用いた太陽電池
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JP5392096B2 (ja) 2014-01-22
TWI404693B (zh) 2013-08-11
EP2246310A4 (fr) 2011-05-11
US20100210443A1 (en) 2010-08-19
US8349751B2 (en) 2013-01-08
CN101959819A (zh) 2011-01-26
EP2246310B1 (fr) 2014-04-16
JPWO2009096611A1 (ja) 2011-05-26
KR20100086005A (ko) 2010-07-29
KR101273782B1 (ko) 2013-06-12
EP2246310A1 (fr) 2010-11-03
TW200951090A (en) 2009-12-16

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